Method of manufacturing magnetic recording medium

ABSTRACT

A method of manufacturing a magnetic recording medium by using an in-line sputtering apparatus to successively form, on a substrate, at least one underlying layer, a first magnetic CoPt-based film, a nonmagnetic intermediate film, and a second magnetic CoPt-based film. The underlying film and/or the nonmagnetic film, which are in contact with the first magnetic film, are deposited at a low sputtering power between 100 and 1000 watts to improve the magnetic properties of the magnetic recording medium. Low power sputtering is also effective to improve the distribution of difference of the crystal lattice spacings between the nonmagnetic intermediate film and the first magnetic film and between the underlying layer and the first magnetic film.

This is a continuation of application Ser. No. 08/575,019 filed Dec. 19,1995 now U.S. Pat. No. 5,746,893.

BACKGROUND OF THE INVENTION

The present invention relates to a method of manufacturing magneticrecording media, such as magnetic disks and magnetic tapes.

Magnetic recording technology has a long history and is based onestablished techniques. The development of an information-based societyin recent years has accelerated the development of magnetic recordingmedia of higher density with improved properties. Such technology hasbecome more and more important.

In particular, a thinner recording layer has been used for higherrecording density in the field of magnetic disks (e.g., hard disks andfloppy disks) used as peripheral storage devices. The Age of Thin FilmMedia using a magnetic thin film has begun. Important challenges are howto ensure the reliability of data stored thereon with a higher recordingdensity and how to make such media suitable for mass-production at a lowmanufacturing cost.

One of the thin film recording layers meeting such requirements consistsof a magnetic layer of a cobalt-platinum (CoPt) based alloy having ahigh coercive force, which is divided into two magnetic films by anonmagnetic layer of chromium (Cr) for the reduction of noise duringreproduction. More specifically, the resultant medium is formed from amagnetic CoPt film, a nonmagnetic Cr film, and another magnetic CoPtfilm in this order. It is also known that an underlying layer of Crprovides a favorable crystalline structure for the magnetic CoPt filmwhen placed under the thin film recording layer (as disclosed inJapanese Patent Laid-Open No. 2-210614).

However, the above-mentioned magnetic recording medium with theunderlying Cr layer, magnetic CoPt film, nonmagnetic Cr film, andmagnetic CoPt film placed in this order exhibits insufficient orunsatisfactory properties for a recording medium, such as coerciveforce, reproduction output voltage of a magnetic head (product ofresidual magnetization and film thickness of the magnetic layer), andsignal-to-noise ratio when it is manufactured with an in-line sputteringapparatus.

In addition, it has been found that the magnetic recording medium havingthe above-mentioned structure which is called a double layer structure,shows coercive force in comparison with a single magnetic layer andshows poor overwriting properties.

On the other hand, it is known that a higher coercive force can beachieved by using chromium as the underlayer of the magnetic layer, suchas CoNiCr alloy or CoCrTa alloy (see, for example, IEEE Transactions onMagnetic, Vol. MAG-3, No. 3 (1967), pages 205-207).

However, the magnetic CoPt alloy layer causes poor orientation of C-axisof h.c.p. structure when only chromium (Cr) is used as an underlayer.This is because the lattice constant of the magnetic CoPt-based alloylayer is larger than the crystalline lattice constant of theconventional magnetic layer of the CoNiCr alloy or the CoCrTa alloy. Asa result, the magnetic CoPt-based layer is not completely matched inatomic alignment with the underlying layer of the single component ofCr. This badly affects the orientation of the C-axis.

In order to overcome this problem, U.S. Pat. No. 4,652,499 proposes toadd a second or different metal to the Cr underlayer to improve thelattice constant. The orientation along the C-axis can be improved forthe magnetic layer in a film interface or boundary by means of changingthe lattice constant of the alloy underlayer by addition of thedifferent metal to the Cr alloy.

The present inventors have found, as a result of detailed consideration,that the resultant recording medium has a significantly larger noise asa result of the addition of the different metal to the underlying Crlayer.

SUMMARY OF THE INVENTION

An object of the present invention is to provide a method ofmanufacturing a magnetic recording medium which has improved properties,such as coercive force, reproduction output voltage of a magnetic headand signal-to-noise ratio.

Another object of the present invention is to provide a method ofmanufacturing a magnetic recording medium which has good over-writingproperties and which can reduce noise.

It is yet another object of the present invention to provide a magneticrecording medium and a method of manufacturing the magnetic recordingmedium which has two or more magnetic CoPt-based alloy layers separatedfrom each other by a nonmagnetic intermediate layer.

In order to achieve the above-mentioned objects, the present inventorshave made a great number of studies. As a result, it was found that thecoercive force and the signal-to-noise ratio are deteriorated due to thecontamination of H₂ O, O₂, and/or N₂ into the nonmagnetic Cr layer whichare adhered to a shield plate or a substrate holder (pallet) that ismoved towards and between targets during the deposition of thenonmagnetic Cr layer when an in-line sputtering apparatus is used. Inaddition, it was also found that use of the in-line sputtering apparatusdeteriorates the film performance of the nonmagnetic layer, and in turndeteriorates the film performance of the magnetic CoPt layer formed onthe nonmagnetic layer.

Further studies showed that impurities can be reduced in the nonmagneticlayer when the in-line sputtering apparatus is driven at low power. Thisshows that the resultant nonmagnetic layer has good film performance,which improves the magnetic CoPt layer formed on the nonmagnetic layer.

The inventors' experimental studies have been conducted to search for anoptimum material which is suitable for the nonmagnetic layer and whichcan be deposited by sputtering at low power within the in-lineapparatus. The studies indicated that a Cr alloy as the nonmagneticlayer can achieve a higher recording density by the use of a relativelythin film thickness with necessary coercive force maintained and thatthe resultant magnetic recording medium has superior propertiesincluding a superior coercive force and signal-to-noise ratio. In otherwords, it was found that when the nonmagnetic film of the Cr alloy iscontinuously deposited along with the magnetic films on both sidesthereof within the in-line sputtering apparatus, the resultantnonmagnetic Cr alloy film has a better film performance and serves toform a magnetic recording medium having superior properties such as thecoercive force. In brief, it was found that the combination of thenonmagnetic Cr alloy film and the in-line sputtering makes it possibleto manufacture a magnetic recording medium having superior properties.

This applies to the relationship between the underlying Cr layer and themagnetic CoPt layer in contact with the underlying layer. The presentinvention was thus completed.

More specifically, a method of manufacturing a magnetic recording mediumaccording to the present invention comprises the steps of successivelydepositing, on a substrate, at least one or more underlying layers and amagnetic layer of a CoPt-based alloy, a nonmagnetic film of a Cr-basedalloy, and a magnetic layer of CoPt-based alloy. The method furthercomprises the step of depositing the underlying layer and/ornon-magnetic film which are brought into contact with the magnetic layerat a low power range between 100 and 1000 watts.

Furthermore, the present inventors have experimented with variousmagnetic record media. In a magnetic recording medium having two or moremagnetic CoPt-based alloy layers divided by a nonmagnetic intermediatelayer, the coercive force and the over-writing properties were degradedin dependency upon the composition of the film material and depositionconditions for the film formed between the magnetic layers. It was alsofound that when the CoPt-based alloy is used for the magnetic layer, thenoise of the medium can be reduced without seriously affecting thecoercive force and the over-writing properties. This serves to reducethe difference between the crystal lattice spacing of the (002) plane ofthe magnetic CoPt-based alloy layer and the crystal lattice spacing ofthe (110) plane of the underlying nonmagnetic Cr alloy layer depositedjust beneath that magnetic layer, when an alloy based on Cr and Mo isused for the nonmagnetic intermediate layer separating the magneticlayer.

In the course of the examinations of the present inventors, it has beenconfirmed by a transmission electron microscope that addition of adifferent metal (e.g., Mo) to the underlying Cr layer causes variousparticle sizes of crystals to grow and deteriorates the formation ofcrystals. More specifically, growth of the magnetic CoPt-based alloylayer (such as CoPtCr), laminated on the underlying Cr alloy layer, isadversely affected by the particle sizes and the non-uniformity of thecrystals in the underlying layer. In other words, the non-uniformity ofthe particle sizes of the crystals in the underlying layer results innon-uniformity of the crystals in the magnetic layer. It has beenconfirmed that such non-uniformity in the magnetic layer gives rise toan increase of noise in the magnetic recording medium.

Considering the above, a second underlying film was laminated on anunderlying layer or film which is formed by crystals having uniformparticle sizes and good crystallinity. In this case, the secondunderlying film was formed by a Cr alloy of Cr and a different metal.The underlying layer of two films was, however, not enough for noisereduction of the medium.

With this knowledge, the present inventors made further examinations andstudies. It was found that the noise of the medium can be remarkablyreduced by adjusting or controlling the difference between the crystallattice spacing of the (002) planes of the magnetic CoPt-based alloylayer and the crystal lattice spacing of the (110) planes of theunderlying Cr alloy (the combination of Cr and the different metal addedthereto) film which provides an uppermost layer or surface of theunderlying layer. IN other words, the coercive force and angle ratio canbe improved and the noise of the medium reduced by decreasing thedifference between the crystal lattice spacing of the (002) planes ofthe magnetic CoPt-based alloy layer and the crystal lattice spacing ofthe (110) planes of the uppermost Cr alloy film.

It is not necessarily optimum that there is no difference between thecrystal lattice spacing of the (002) planes of the magnetic CoPt-basedalloy layer and that of the (110) planes of the underlying Cr alloy filmor the Cr alloy intermediate film. Various experiments and examinationsindicated that a small difference is preferable in view of the reductionof the noise. More specifically, control of the C-axis orientation ofthe magnetic layer within a certain range results in a reduction of thenoise of the medium. The deposition at low sputtering power serves toadjust the crystal lattice spacing of the (002) planes of the magneticCoPt-based alloy layer to that of the (110) planes of the underlying Cralloy layer.

According to another aspect of this invention, a method is provided foruse in manufacturing a magnetic recording medium which includes amagnetic layer. The magnetic layer comprises first and second magneticfilms each of which essentially comprises Co and Pt and a nonmagneticintermediate film which is interposed between the first and the secondmagnetic films and which essentially comprises Cr and Mo. Each of thefirst and the second magnetic films is characterized by a hexagonalclose-packed (hcp) crystal structure having (002) planes remote fromeach other by a first crystal lattice plane spacing d.sub.(002) whilethe nonmagnetic intermediate film is characterized by a body-centeredcubic (bcc) crystal structure having (110) planes distant from eachother by a second crystal lattice plane spacing d.sub.(110). The methodcomprises the step of successively depositing the nonmagneticintermediate film and the second magnetic film at low power such thatthe difference between the first crystal lattice plane spacingd.sub.(002) and the second crystal lattice plane spacing d.sub.(110)falls within a range between 0.002 and 0.032 angstrom.

BRIEF DESCRIPTION OF THE DRAWING

FIG. 1 is a plane view of an in-line sputtering apparatus for magneticdisks, which is used to achieve the method of manufacturing a magneticrecording medium according to the present invention;

FIG. 2 is a front view of a pallet on which glass substrates are placed;

FIGS. 3 (a) and (b) are views for use in describing the sputteringconditions around targets; and

FIG. 4 is a schematic sectional view of a magnetic recording mediummanufactured according to the present invention.

DESCRIPTION OF PREFERRED EMBODIMENTS

The present invention will be described in detail hereinunder.

A magnetic recording medium according to a first embodiment of thepresent invention is manufactured by using an in-line sputteringapparatus 10 illustrated in FIG. 1.

The in-line sputtering apparatus 10 comprises a pallet load chamber(loadlock chamber) 11, a sputtering chamber (vacuum chamber) 12, and apallet unload chamber (loadlock chamber) 13, all of which are connectedin line with one another through partitioning plates 14, 21 and 23.Briefly stated, pallets are fed from the pallet load chamber 11 to thesputtering chamber 12, where multiple layers are deposited successivelyon a substrate. The pallets are transferred from the sputtering chamber12 to the pallet unload chamber 13. This apparatus is of a loadlock typeand therefore carries out continuous operation without exposing thesputtering chamber 12 to the air.

Pairs of targets 15a through 15g of predetermined materials are arrangedin a predetermined order within the sputtering chamber 12 so as tomanufacture the magnetic recording medium. Shield plates 16a through 16gpartially surround the pairs of targets 15a through 16g to avoid anyadverse influence of plasma generated from the adjacent targets.

A d.c. magnetron method is used for the sputtering, and the optimumsputtering condition is achieved by controlling the magnetic field bythe use of magnetron cathodes of plate shapes which have electromagnets.

As shown in FIG. 2, an upright self-supporting pallet 18 which holds aplurality of substrates 17 is allowed to pass between the pairs of thetargets 15a through 15g arranged on both side walls of the sputteringchamber 12. This movement of the pallet 18 enables simultaneousdeposition of each film on both sides of each substrate 17.

Heaters 19 and 20 are provided for controlling the temperature of thesubstrate during the deposition. The temperature of the substrate 17upon sputtering affects the coercive force and it is preferable that theheaters 19 and 20 are adjusted to 200° C. or higher during sputtering.

Properties of the Co alloy-based magnetic film deposited through thesputtering vary considerably, depending on the Ar gas pressure or thetemperature of the substrate. Accordingly, control of these factors isimportant. Though it has not been determined exactly because it dependson the material used for the film, the Ar gas pressure upon sputteringpreferably falls within a range between 1×10⁻³ and 1×10⁻² Torr.

The in-line sputtering apparatus used for the present invention is notlimited to the one illustrated in FIG. 1. It is apparent that thepresent invention can also be applied to any in-line sputteringapparatus (such as an in-line sputtering apparatus of other types usedfor magnetic disks or magnetic tapes) which have elements, such as thepallets and the shield plates, which are adjacent to the targets andwhich act as impurity sources.

In the present invention, a magnetic recording medium is manufactured bysuccessively depositing, on the substrate, at least one or moreunderlying layers, a magnetic CoPt-based layer, a nonmagnetic Cr-basedlayer, and a magnetic CoPt-based layer within the above-mentionedin-line sputtering apparatus.

The substrate used may be, for example, a glass substrate, acrystallized glass substrate, a surface-reinforced glass substrate, analuminum substrate, an aluminum alloy substrate, a ceramic substrate, aplastic substrate, a Si substrate, a Ti substrate, or a carbonsubstrate.

In the present invention, one or more underlying layers are deposited onthe above-mentioned substrate with the in-line sputtering apparatus.

In this event, the underlying layer (the uppermost layer or the surfaceof the underlying layer) to be brought into contact with the magneticlayer is required to be deposited at a low sputter power. The reasonwill be described with reference to FIGS. 3(a) and 3(b). Herein, it isto be noted that FIGS. 3(a) and 3(b) show two views describing thesputtering conditions around a target 15 and a pallet 18. Whenunderlying the layer which is to be brought into contact with themagnetic layer is deposited at low sputtering power, the particlesemitted from the target 15 during sputtering have a high probability ofreaching the substrate pallet 18 without being scattered, as shown inFIG. 3(b). As a result, the particles are decreased in number ascompared to the case where sputtering is carried out at high sputteringpower as shown in FIG. 3(a). In other words, a large amount of particlesare emitted from the target 15 and scattered in various directions, asillustrated in FIG. 3(a), when the sputtering is carried out at highsputtering power. Accordingly, such low power sputtering makes itpossible to reduce the amount of impurities, such as H₂ O, O₂, and/orN₂, which are attached to the shield plate 16 and/or the pallet 18 andwhich are sputtered by the particles emitted from the targets to bedirected to the underlying layer. The resultant underlying film includesa small amount of the impurities and therefore has excellent properties.This ensures favorable crystal growth of the magnetic film formed on theunderlying layer and accomplishes improved magnetic properties such asthe coercive force.

The crystal growth of the magnetic layer becomes poor if the underlyinglayer contacted with the magnetic layer is deposited at a sputteringpower lower than 100 watts. On the other hand, sputtering power which ishigher than 1000 watts brings about deterioration of the magneticproperties due to mixture of impurity gases into the underlying layer.The sputtering power is thus preferably selected within the rangebetween 100 and 1000 watts. More preferably, the sputtering power mayfall within a range from 300 to 700 watts. The sputtering currentlydensity is preferably selected within the range from 0.9 to 10 W/cm² forthe same reason.

As the sputtering power becomes low, the sputtering rate (depositionrate) becomes slow in proportion to the sputtering power. It might thusbe considered that the sputtering rate also contributes to theimprovement of the film properties or performance of the underlyinglayer. In this respect, the sputtering rate upon deposition of theunderlying layer contacted with the magnetic layer may preferably becontrolled within a range from 150 to 1500 angstroms/min., and morepreferably from 450 to 1000 angstroms/min.

Herein, the underlying layer in contact with the magnetic layer ispreferably formed by an alloy based on Cr. This is because the alloybased on Cr can obtain the coercive force that is required to achieve ahigh recording density with a relatively thin thickness. Therefore, suchan underlying layer is not deteriorated in the magnetic properties, evenwhen it is deposited in low sputtering power.

The layer of the alloy based on Cr, which serves as the underlying layerin contact with the magnetic layer, may have a film thickness between 10and 100 angstroms in consideration of the magnetic properties of theresultant magnetic recording medium.

Such alloys based on Cr may be, for example, alloys of CrMo, CrV, andCrTa and other alloys containing, together with the above-mentionedalloys, one or two elements selected from the group consisting of Zr, W,B, Nb, Ta, Fe, Ni, Re, Ce, Zn, P, Si, Ga, Hf, Al, and Ti. Of thesealloys, CrMo, CrV, CrMoZr, and CrTa alloys are very preferable becauseof remarkable improvements of magnetic properties. The content ofelements other than Cr in the Cr-based alloy is typically around 10 at.%, taking into consideration the coherency of the magnetic layer latticespacing.

The underlying layer may consist of two or more layers or film and willhereinunder be collectively called an underlying lamina. For example, aCr layer may underlie the Cr-based alloy layer in contact with themagnetic layer. Alternatively, if a glass substrate is used, theunderlying lamina may be composed of three layers successively formed onthe glass substrate. Specifically, the underlying lamina may be composedof an Al layer, a Cr layer, and a Cr-based alloy layer.

The present invention, the magnetic layer is formed on theabove-mentioned underlying lamina with the in-line sputtering apparatusand may consist of the magnetic CoPt-based film, the nonmagneticCr-based film, and the magnetic CoPt-based film.

In this event, the nonmagnetic Cr-based film is deposited at lowsputtering power. This reason is similar to that mentioned in relationto the magnetic layer (magnetic film) and the underlying layer incontact with the above-mentioned magnetic layer. More particularly, thenonmagnetic film is deposited at low sputtering power to reduce theamount of impurities undesirably mixed into the underlying layer. Thenonmagnetic film thus has a good film performance. This enables not onlyfavorable crystal growth of the magnetic film formed on the nonmagneticfilm but also improvement of magnetic properties, such as the coerciveforce.

As mentioned in conjunction with the underlying layer, the crystalgrowth of the nonmagnetic layer becomes poor if the nonmagnetic film isdeposited at a sputtering power lower than 100 watts. On the other hand,a sputtering power of higher than 1000 watts results in deterioration ofthe magnetic properties due to undesirable mixture of impurity gases.The sputtering power is thus preferably selected within the range from100 to 1000 watts. More preferably, the sputtering power falls withinthe range from 300 to 700 watts. The sputtering current density ispreferably in the range of from 0.9 to 10 W/cm² for the same reason.

Like in the underlying layer, it is preferable that the nonmagnetic filmis deposited at a deposition rate between 150 and 1500 angstroms/min.,more preferably between 450 and 1000 angstroms/min.

The nonmagnetic film is preferably formed by an alloy based on Cr, likethe underlying layer. This is because the alloy based on Cr enablesobtainment of the coercive force which is required to achieve a highrecording density with a relatively small film thickness. In addition,such a nonmagnetic film using an alloy based on cr never deterioratesthat magnetic properties even when the deposition is conducted at lowsputtering power.

The nonmagnetic film of the alloy based on Cr may have a film thicknessbetween 10 and 100 angstroms, taking into consideration the magneticproperties of the resultant magnetic recording medium.

Such alloys based on Cr may be, for example, alloys of CrMo, CrV, andCrTa and other alloys containing, together with the above-mentionedalloys, one or two elements selected from the group consisting of Zr, W,B, Nb, Ta, Fe, Ni, Re, Ce, Zn, P, Si, Ga, Hf, Al, and Ti. Of thesealloys, CrMo, CrV, CrMoZr, and CrTa alloys are very preferable becauseof remarkable improvement of magnetic properties. The content ofelements other than Cr in the Cr-based alloy is preferably determined inconsideration of the coherency of the magnetic layer lattice spacing.

It is preferable that the total amount of Co and Pt in the magneticCoPt-based film is equal to or greater than 70 (at. %) to providesufficient coercive force. In addition, no limitation is imposed on theratio between Co and Pt. However, it is preferable that the ratio Pt/Co(at. %) is in a range from 0.06 to 0.2 from the viewpoints of improvingthe coercive force, reducing the noise, and reducing costs.

Other components may be contained in addition to Co and Pt in themagnetic layer. For example, the magnetic layer may contain at least oneelement selected from the group consisting of Cr, Ta, B, O, N, Nb, Mn,Zn, W, Pb, Re, V, and Zr. Specifically, the magnetic layer may be formedby a CoPtCr alloy, a CoPtTa alloy, a CoPtCrB alloy, a CoPtCrTa alloy, ora CoPtCrNi alloy.

Each of the magnetic films separated by the nonmagnetic film may beformed either by the same material or a different material and may beeither identical with or different from each other in thickness. Inaddition, the magnetic layer may have a plurality of magnetic films(e.g., five films) structured by alternative lamination of thenonmagnetic and magnetic films.

A protection layer and a lubrication layer are successively deposited onthe above-mentioned magnetic layer.

The protective layer is formed on the magnetic layer for the purpose ofprotecting the magnetic layer from being destroyed due to contactoperation of a magnetic head.

As the protection layer, a Cr layer, a Cr alloy layer, a carbon layer, azirconium layer, or a silica layer can be used. The protection layer maybe deposited successively along with the other layers, such as themagnetic layer, by the use of the in-line sputtering apparatus. Theprotection layer may have a single-film structure, or may have aplurality of films which may be formed either by the same material or bydifferent materials.

Another protection layer may be stacked on the above-mentionedprotection layer. For example, tetraalkoxysilane which is diluted withan alcoholic solvent is coated on the above-mentioned protection layerand is fired to form a silicon oxide (SiO₂) film which serves as anotherprotection layer.

With this structure, the Cr layer or the like provides both shockresistance and chemical protection, while the SiO₂ layer provides bothwear resistance and corrosion resistance.

The lubricant layer is formed on the protection layer so as to reducefrictional resistance between the magnetic head and a surface of theresultant medium. The lubricant layer may typically be applied in thefollowing manner. A liquid lubricant of, for example, perfluoropolyether(PEPE) is prepared and diluted with, for example, a Freon-based solvent.Thereafter, the resultant lubricant is applied on the protection layerby the use of dipping, spin coating, or spraying technique. The coatedfilm may be heated.

The present invention will be described more in detail below inconjunction with a set of examples and comparative examples, taking theabove into account. Herein, it is to be noted that Examples exemplifythe magnetic recording medium according to the above-mentionedembodiment.

EXAMPLE 1

As shown in FIG. 4, Example 1 has a glass substrate 1 and an underlyinglamina 2 on the glass substrate 1. On the underlying lamina 2, a firstmagnetic film 3, a nonmagnetic film 4, a second magnetic film 5, and aprotection layer 6 are successively deposited in this order. Inaddition, a lubricant layer 7 is coated on the protection layer 6. Theillustrated magnetic disk is manufactured through the following steps.

As mentioned before, a magnetic disk with reduced noise is obtained byinterposing the nonmagnetic film 4 between the magnetic CoPt-based films3 and 5 and which exhibits high coercive force. The magnetic disk isfavorably combined with an MR head.

First, a glass substrate with a diameter of 2.5 inches is prepared whichis composed of aluminosilicate glass chemically reinforced by means ofion exchange. Both the front and rear surfaces of the glass substrateare precisely polished to provide mirror surfaces each of which has asurface roughness (Ra) of about 50 angstroms.

As shown in FIG. 2, the above-mentioned glass substrate is mounted ontoa substrate holder or pallet. The pallet 18 is fed to the pallet loadchamber 11 of the in-line sputtering apparatus 10 illustrated in FIG. 1.Subsequently, the pallet load chamber 11 is exhausted from atmosphericpressure to a degree of vacuum which is similar to that of thesputtering chambers (vacuum chambers) 12. Thereafter, a partition wall14 is opened to introduce the pallet 18 into a first one of the vacuumchambers (12a). In this first vacuum chamber 12a, the glass substratemounted on the pallet 18 is heated by a lamp heater 19 at 300° C. forone minute. Then, the pallet 18 is transferred or transported at atransfer speed of 50 cm/min. and allowed to pass between the opposingpairs of the targets 15a and 15b which are kept in discharge states. Thetargets are aligned along the transfer direction of the pallet and aresuccessively arranged in the order of target 15a for aluminum (Al)deposition and target 15b for chromium (Cr) deposition. Therefore, anunderlying Al film 2a of 50 angstroms in thickness and an underlying Crfilm 2b of 1000 angstroms in thickness are successively deposited onboth the front and the rear surfaces of the glass substrate.

Next, the pallet 18 is transferred to a second one of the vacuumchambers (12b) through a port 21. The pallet 18 is heated again by aheater 20 located within the second vacuum chamber 12b. The heattreatment is carried out at 350° C. for 1 minute. Thereafter, the pallet18 is moved at a transfer speed of 50 cm/min. between the pairs oftargets 15c through 15 g held in discharge states. In the second vacuumchamber 12b, targets 15c for CrMo, targets 15d for CoPtCr, targets 15efor CrMo, targets 15f for CoPtCr, and targets 15g for Cr aresuccessively arranged in this order. The films are deposited in theorder of the target arrangement. More specifically, deposition is madeof an underlying CrMo film 2c of 100 angstroms in thickness, a firstmagnetic CoPtCr film 3 of 120 angstroms in thickness, a nonmagnetic CrMofilm 4 of 50 angstroms in thickness, a second magnetic CoPtCr film 5 of120 angstroms in thickness, and a first protection Cr layer 6a of 50angstroms in thickness in this order

The CrMo target 15c was composed of 98 at. % Cr and 2 at. % Mo, whilethe CrMo target 15e was composed of 95 at. % Cr and 5% Mo. In addition,the CrMo targets 15c and 15 3 were sputtered at a power of 500 watts.

The CoPtCr targets 15d and 15f were composed of 78 at. % Co, 11 at. %Pt, and 11 at. % Cr.

Furthermore, the vacuum chamber was finally exhausted to 5×10⁻⁶ Torr andthen Ar gas was introduced. Under the circumstances, sputtering wasconducted at a pressure of 5×10⁻³ Torr.

After completion of deposition based on sputtering, hydrophilication wasconducted by washing the first protection Cr layer 6a with isopropylalcohol (IPA). Thereafter, the substrate was dipped in an organicsilicon compound solution (a solution of water, IPA andtetraethoxysilane) in which fine particles (particle size of 100angstroms) of silica were dispersed. The resultant substrate was firedto form the second protection layer 6b of SiO₂.

Finally, the surface of the second protection layer 6b was dipped into alubricant of perfluoropolyether to form the lubricant layer 7.

The magnetic disk so obtained was tested for coercive force, the productof residual magnetization and film thickness, and signal-to-noise ratio.The results are shown in Table 1 below. Table 1 also shows thedifference (d.sub.(002) -d.sub.(110), obtained by subtracting thecrystal lattice spacing of BCC (110) planes in the nonmagnetic film 4 ofa material based on Cr and Mo from the crystal lattice spacing of HCP(002) planes in the second magnetic film 5. As enumerated in Table 1,the distance is less than 0.030 angstrom.

COMPARATIVE EXAMPLE 1

Comparative Example 1 was prepared by manufacturing a magnetic disk in amanner similar to that of Example 1. However, Comparative Example 1 wasmanufactured by supplying both CrMo targets 15c and 15e with asputtering power of 2000 watts. Similar tests were conducted and theresults of the tests are shown in Table 1.

COMPARATIVE EXAMPLE 2

Comparative Example 2 was manufactured in a manner similar to that ofComparative Example 1. However, Cr targets were used in place of theCrMo targets 15c and 15e. Similar tests and their results are shown inTable 1.

EXAMPLES 2 THROUGH 4

Examples 2 through 4 were manufactured like Example 1. It is, however,noted that both CrMo targets 15c and 15e were supplied with sputteringpower of 200 watts, 800 watts, and 1000 watts in Examples 2, 3, and 4,respectively.

COMPARATIVE EXAMPLES 3 AND 4

Comparative Examples 3 and 4 were manufactured by supplying both theCrMo targets 15c and 15e with sputtering power of 50 watts and 1500watts, respectively.

EXAMPLES 5 THROUGH 7

Examples 5 through 7 were manufactured by the use of CrMoZr targets (Cr90 at. %, Mo 8 at.T, and Zr 2 at. %) (Example 5), CrV targets (Cr 95 at.%, and V 5 at. %) (Example 7). Such targets were used in place of theCrMo targets 15e. Examples 5 through 7 had magnetic propertiesenumerated in Table 1.

EXAMPLES 8 THROUGH 11

Examples 8 through 11 were manufactured in a manner that was similar tothat of Example 1 except that the CrMo target 15e wee composed of Cr 95at. % and Mo 5 at. % (Example 8), Cr 90 at. % and Mo 10 at. % (Example9), Cr 80 at. % and Mo 20 at. % (Example 10), and Cr 60 at. % and Mo 40at. % (Example 11). Examples 8 through 11 were evaluated and hadmagnetic properties shown in Table 1.

EXAMPLES 12 THROUGH 18

Examples 12 through 18 were manufactured in a manner that was similar tothat of Example 1 except that the targets as shown in the column "Note"of Table 1 were used in place of the CoPtCr targets 15d and 15f. Similarevaluation was made in conjunction with Examples 12 through 18.

                  TABLE 1    ______________________________________                       S/N    d.sub.(002) -    Hc         Mr · δ                       ratio  d.sub.(110)                                    NOTE    ______________________________________    Example 1            1900   0.97    33.7 0.030    Compara-            1950   1.00    29.5       Sputtering Power    tive                              200 watts    Example 1    Compara-            1650   0.86    31.5       Nonmagnetic Cr film    tive    Example 2    Compara-            1900   0.95    27.8       Sputtering Power    tive                              50 watts    Example 3    Example 2            1900   0.97    33.4 0.029 Sputtering Power                                      200 watts    Example 3            1950   0.94    34.0 0.030 Sputtering Power                                      800 watts    Example 4            2000   0.92    33.7 0.030 Sputtering Power 1000                                      watts    Compara-            1800   0.82    29.1       Sputtering Power 1500    tive                              watts    Example 4    Example 5            2050   0.97    35.0 0.020 Cr 90, Mo 8, Zr 2    Example 6            1850   0.95    33.3 0.032 Cr 95, V5    Example 7            1800   0.95    33.3 0.019 Cr 95, Ta 5    Example 8            1950   1.00    33.8 0.030 Cr 95, Mo 5    Example 9            1950   0.97    33.7 0.019 Cr 90, Mo 10    Example 10            1900   0.97    33.9 0.006 Cr 80, Mo 20    Example 11            1730   0.92    32.3 0.002 Cr 60, Mo 40    Example 12            1880   1.10    32.7 0.031 Co 85, Pt 10, Cr 5    Example 13            2130   0.90    33.1 0.021 Co 74, Pt 15, Cr 5    Example 14            2130   0.68    34.3 0.018 Co 71, Pt 12, Cr 17    Example 15            2100   0.63    35.6 0.028 Co 68, Pt 8, Cr 18, Ta 6    Example 16            2020   0.91    35.1 0.027 Co 72, Pt 10, Cr 14, Ta 4    Example 17            1850   1.15    32.4 0.029 Co 88, Pt 10, Ta 2    Example 18            1910   0.97    32.0 0.031 Co 83, Pt 12, Ta 5    ______________________________________      Units: Hc(Oe), Mr · δ(memu/cm.sup.2), S/N ratio (dB)

As is apparent from Table 1, Comparative Example 1 exhibited a lowsignal-to-noise ratio and caused a large medium noise to occur. This isbecause the nonmagnetic film is deposited at high sputtering power.

In addition, Comparative Example 2 exhibited a low coercive forcebecause the nonmagnetic film of Cr is deposited at high sputteringpower.

According to Examples 1 through 18, the coercive force, the product ofresidual magnetization and film thickness, and the signal-to-noise ratiocan be adjusted to more preferable values by means of changing thesputtering power, the material and composition of the nonmagnetic film,and those of the magnetic films.

EXAMPLES 19 THROUGH 21 AND COMPARATIVE EXAMPLES 5 AND 6

Examples 19 through 21 and Comparative Examples 5 and 6 wee manufacturedin a manner which was similar to that of Example 1 except that the CrMotargets 15c and 15e were driven by the sputtering power and thesputtering power density both of which were varied as indicated in thecolumn "Note" of Table 2. Similar results are shown in Table 2.

                  TABLE 2    ______________________________________                       S/N    d.sub.(002) -    Hc         Mr · δ                       ratio  d.sub.(110)                                    NOTE    ______________________________________    Compara-            1900   0.95    28.8       Sputtering Power Density    tive                              0.5    Example 5    Example 19            1900   0.96    30.5 0.029 Sputtering Power Density                                      1.0    Example 20            1900   0.97    33.7 0.030 Sputtering Power Density                                      5.0    Example 21            2000   0.95    32.9 0.030 Sputtering Power Density                                      10    Compara-            1800   0.82    29.1       Sputtering Power Density    tive                              15    Example 6    ______________________________________      Unit: Sputtering Power Density (W/cm.sup.2)

EXAMPLES 22 THROUGH 24 AND COMPARATIVE EXAMPLES 7 AND 8

Examples 22 through 24 and Comparative Examples 7 and 8 weremanufactured by changing the deposition or sputtering rates as shown inTable 3 on sputtering the CrMo targets 15c and 15e. Such a change of thedeposition rates can be accomplished by varying the sputtering powergiven to the CrMo targets 15c and 15e. The magnetic properties are shownin Table 3.

                  TABLE 3    ______________________________________                       S/N    d.sub.(002) -    Hc         Mr · δ                       ratio  d.sub.(110)                                    NOTE    ______________________________________    Compara-            1900   0.95    28.1       Sputtering Rate 100    tive    Example 7    Example 22            1900   0.96    32.2 0.030 Sputtering Rate 180    Example 23            2000   0.95    32.9 0.030 Sputtering Rate 1000    Example 24            1900   0.91    31.0 0.032 Sputtering Rate 1400    Compara-            1750   0.80    27.9       Sputtering Rate 1600    tive    Example 8    ______________________________________      Unit: Sputtering Rate (angstrom/min.)

                  TABLE 3A    ______________________________________             Differences of Crystal Lattice Spacing             (d.sub.(002) -d.sub.(110))             Underlying Layer/                        Nonmagnetic Film/             1st Magnetic Film                        2nd Magnetic Film    ______________________________________    Example 1  0.031        0.030    Example 2  0.030        0.029    Example 3  0.031        0.030    Example 4  0.031        0.030    Example 5  0.021        0.020    Example 6  0.031        0.032    Example 7  0.031        0.019    Example 8  0.031        0.030    Example 9  0.031        0.019    Example 10 0.031        0.006    Example 11 0.031        0.002    Example 12 0.032        0.031    Example 13 0.023        0.021    Example 14 0.019        0.018    Example 15 0.029        0.028    Example 16 0.028        0.027    Example 17 0.030        0.029    Example 18 0.032        0.031    Example 19 0.030        0.029    Example 20 0.031        0.030    Example 21 0.031        0.030    Example 22 0.031        0.030    Example 23 0.031        0.030    Example 24 0.032        0.032    ______________________________________

As are apparent from Tables 2 and 3, Examples 19 through 24 andComparative Examples 5 through 8 show that the coercive force, theproduct of residual magnetization and film thickness, and thesignal-to-noise ratio can be adjusted to preferable values by means ofchanging the sputtering power density and the sputtering rate. In all ofthe Examples above, it is to be noted that the difference (d.sub.(002)-d.sub.(110)) between crystal lattice spacing falls within a range from0.002 to 0.032 angstroms.

Herein, the differences (d.sub.(002) -d.sub.(110)) between thenonmagnetic film 4 and the second magnetic film 5 have been shown inTables 1 to 3 and may be called first differences. Herein, it is to benoted that d.sub.(002) represents a first crystal lattice plane spacingof (002) planes of a hexagonal close-packed (hcp) crystal structure inthe second magnetic film 5 of Co and Pt, while d.sub.(110)) represents asecond crystal lattice plane spacing of (110) planes in the nonmagneticfilm 4 of Cr and Mo.

More specifically, such differences have been also measured inconnection with the underlying layer 2c and the first magnetic film ofeach of Examples 1 through 24 and may be referred to as seconddifferences. The second differences have been shown in the first columnof Table 3A together with the second differences (d.sub.(002)-d.sub.(110)) shown in the second column of Table 3A. As readilyunderstood from Table 3A, the second differences (d.sub.(002)-d.sub.(110)) between the underlying layer 2c and the first magneticfilm of each of Examples 1 through 24 lie within a range between 0.002and 0.032 angstrom like the first differences (d.sub.(002) -d.sub.(110))between the nonmagnetic film 4 and the second magnetic film 5.

Thus, processing is made as regards Examples 1 to 24 so that both thefirst and the second differences (d.sub.(002) -d.sub.(110)) fall withinthe range between 0.002 and 0.032 angstrom. In other words, the lowpower sputtering mentioned above serves to render each of the first andthe second differences within the above-mentioned range. Accordingly,the low power sputtering is effective to reduce variations of the firstand the second differences within planes. This makes a distribution ofthe differences (d.sub.(002) -d.sub.(110)) uniform in planes and ishelpful to make the quality of the films and the film structuresuniform. In addition, it has been confirmed that Examples 1 through 24have improved magnetic properties, as shown in Tables 1 through 3.

A magnetic recording medium according to a second embodiment of thepresent invention has a similar structure to the one illustrated in FIG.4 although some differences are present between the first and the secondembodiments, as will become clear later.

Example 25 was manufactured in the following manner as the magneticrecording medium according to this embodiment. The glass substrate 1 inExample 25 is composed of aluminosilicate glass and is preciselypolished to provide mirror surfaces which have a surface roughness (Ra)of about 50 angstroms.

The underlying lamina 2 is composed of a thin Al film 2a of 50 angstromsin thickness, a thin Cr film 2b of 600 angstroms in thickness, and thinCrMo film 2c of 50 angstroms in thickness. The thin CrMo film 2ccomprises Cr 98 at. % and Mo 2 at. %.

The first magnetic film 3 and the second magnetic is film 5 are composedof the same material, i.e., a CoPtCr alloy (Co: 78 at. %, Pt: 11 at. %,and Cr: 11 at. %) and are each 120 angstroms in thickness.

The nonmagnetic film, namely, the nonmagnetic intermediate film 4interposed between the first magnetic film 3 and the second magneticfilm 5 is composed of a CrMo alloy (Cr: 98 at. %, and Mo 2 at. %) andhas a thickness of 50 angstroms.

The protection layer 6 is composed of the first protection film 6a andthe second protection film 6b which are successively stacked from theside of the substrate. The first protection film 6a is composed of a Crfilm of 50 angstroms in thickness, and serves as a chemical protectionfilm for the magnetic layer. The other protection film 6b is composed ofa silicon oxide film of 160 angstroms in thickness has hard fineparticles dispersed therein. This second protection film 6b provideswear resistance.

The lubricant layer 7 is composed of perfluoropolyether so as tomitigate contact shock with a magnetic head.

A method of manufacturing the above-mentioned magnetic disk is describedbelow.

The above-mentioned glass substrate is mounted onto a substrate holder(pallet). The pallet 18 is fed to the pallet load chamber 11 of thein-line sputtering apparatus 10 illustrated in FIG. 1. Subsequently, thepallet load chamber 11 is evacuated from the atmospheric pressure to adegree of vacuum similar to that of the sputtering chamber (vacuumchamber) 12. Thereafter, the partition wall 14 is opened to feed thepallet 18 into the first vacuum. chamber 12a. In this first vacuumchamber 12a, the glass substrate mounted on the pallet 18 is heated witha lamp heater 19 at 300° C. for one minute. Then, the pallet 18 istransferred at a transfer speed of 1.2 m/min. and allowed to passbetween the opposing pairs of the targets 15a and then between targets15b which are kept in discharge states under an Ar gas pressure of 5mTorr. The targets are arranged along the transfer direction of thepallet and are formed by the targets 15a for aluminum (Al) depositionand the targets 15b for chromium (Cr) deposition. Therefore, anunderlying Al film 2a and an underlying Cr film 2b are successivelydeposited on both surfaces of the glass substrate in the order of thetargets. The Al targets and Cr targets are supplied with 300 watts and1.0 kilowatts, respectively, during sputtering.

Next, the pallet 18 is transferred to the second vacuum chamber 12bthrough the partition wall 21. The pallet 18 is heated again with aheater 20 located within the second vacuum chamber 12b. The heattreatment is carried out at 375° C. for 1 minute. Thereafter, the pallet18 is transported at a transfer speed of 1.2 m/min. between the pairs oftargets 15c through 15g kept in discharge states. Such discharge statescan be maintained in Ar gas kept at a pressure of 1.3 mTorr. The secondvacuum chamber 12b has an arrangement of targets 15c for CrMo, targets15d for CoPtCr, targets 15e for CrMo, targets 15f for CoPtCr, andtargets 15g for Cr which are located in this order. The films aredeposited in the order of the target arrangement. More specifically, theunderlying CrMo layer 2c, the first magnetic CoPtCr film 3, thenonmagnetic CrMo film 4, the second magnetic CoPtCr film 5, and thefirst protection Cr film 6a are successively deposited on the underlyingCr film 2b.

Sputtering was conducted with a power of 300 watts applied to the CoPtCrtargets and 500 watts to the Cr targets. Furthermore, the vacuum chamberwas finally exhausted to 5×10⁻⁶ Torr and Ar gas was introduced to 5×10⁻⁶Torr. Under the circumstances, sputtering is carried out in the secondvacuum chamber 12b.

After completion of deposition through sputtering, the first protectionlayer 6a and the second protection layer 6b are formed in the mannerdescribed above.

Finally, the lubricant layer 7 is formed on the second protection layer6b like in the first embodiment.

The magnetic disk so obtained was subjected to operational tests with afloating distance kept at 0.075 μm or less. The results were good. Inaddition, the coercive force (Hc), the product (Mrδ) of residualmagnetization and film thickness, and the signal-to-noise ratio weretested in connection with the above-mentioned magnetic disk. The resultsare shown in Table 4.

Furthermore, Table 4 also shows compositions and film thicknesses of theunderlying CrMo layer 2c and of the nonmagnetic intermediate CrMo film4, and the substrate heating temperature and Ar gas pressure uponformation of the underlying CrMo layer 2c and the nonmagneticintermediate CrMo film 4. Moreover, differences (d.sub.(002)-d.sub.(110)) are also shown which are obtained by subtracting thecrystal lattice spacing of the (110) planes in the underlying CrMo layer2c (in contact with the magnetic CoPtCr film 3) from the crystal latticespacing of the (002) planes in the magnetic CoPtCr film 3. In addition,differences (d.sub.(002) -d.sub.(110)) are enumerated which are obtainedby subtracting the crystal lattice spacing of the (110) planes in thenonmagnetic intermediate CrMo film 4 from the crystal lattice spacing ofthe (002) planes in the magnetic CoPtCr film 5.

It is noted that the differences (d.sub.(002) -d.sub.(110)) obtainedfrom the underlying CrMo layer 2c and the magnetic CoPtCr film 3 wereidentical with the differences (d.sub.(002) -d.sub.(110)) obtained fromthe nonmagnetic intermediate CrMo film 4 and the magnetic CoPtCr film 5.This is because the underlying layer 2c, the nonmagnetic intermediatefilm 4, the magnetic film 3, and the magnetic-film 5 were manufacturedunder the same conditions. Taking this into consideration, Table 4 thusshows only one of two values obtained for each example. Likewise, thisis also true of Table 5.

The signal-to-noise ratio was measured by the use of a thin film head.Specifically, recording and reproduction outputs were measured at atrack recording density of 110 kfci with a relative rate kept at 5.0 m/sbetween the thin film head and the disk and the magnetic head floatingdistance held at 0.060 μm. In addition, the noise spectrum of themagnetic disk was measured during signal recording and reproduction onthis magnetic disk by a spectrum analyzer which had a carrier frequencyand a measuring bandwidth set to 13.5 MHz and 27 MHz, respectively. TheMR head used in the above-mentioned measurements had a recording trackwidth of 4.2 μm, a reproduction track width of 3.5 μm, a recording gaplength of 0.43 μm, and a reproduction gap length of 0.31 μm.

EXAMPLES 26 THROUGH 53

Examples 26 through 49 were manufactured in a manner which is similar tothat of Example 25 except that process conditions were changed fromthose of Example 25 in connection with the compositions and the filmthicknesses of the underlying CrMo layer 2c, those of the nonmagneticintermediate CrMo film 4, the substrate heating temperature, and the Argas pressures upon formation of the underlying CrMo layer 2c and thenonmagnetic intermediate CrMo film 4, as enumerated in Table 4. Inaddition, Examples 50 through 53 were similar to those of the otherexamples except that the underlying CrMo layer 2c and the nonmagneticintermediate CrMo film 4 were formed by CrMoZr alloy and had filmthicknesses of 50 angstroms, and that the composition of each layer waschanged from the other examples, as shown in Table 5.

The magnetic disks according to Examples 26 through 53 were subjected tooperational tests with the floating distance kept at 0.075 μm or less.In addition, the coercive force (Hc), the product (Mrδ) of residualmagnetization and film thickness, and the signal-to-noise ratio werealso measured in connection with Examples 26 through 53. Thesignal-to-noise ratio was measured in the same manner as in Example 25.All of the test results are shown in Tables 4 and 5.

Furthermore, Tables 4 and 5 also show the compositions and the filmthicknesses of the underlying CrMo layer 2c, those of the nonmagneticintermediate CrMo film 4, the substrate heating temperature and the Argas pressure during formation of the underlying CrMo layer 2c and thenonmagnetic intermediate CrMo film 4, and the differences (d.sub.(002)-d.sub.(110)) obtained by subtracting the crystal lattice spacing of the(110) planes in the underlying CrMo layer 2c from the crystal latticespacing of the (002) planes in the magnetic CoPtCr film 3, and thedifferences (d.sub.(002) -d.sub.(110)) obtained by subtracting thecrystal lattice spacing of the (110) planes in the nonmagneticintermediate CrMo film 4 from the crystal lattice spacing of the (002)planes in the magnetic CoPtCr film 5. At any rate, the above-mentioneddifferences in all of Examples fall within a range between 0.002 and0.032 angstrom. This applies to the following examples.

                                      TABLE 4-1    __________________________________________________________________________          Magnetic Layer       Nonmagnetic                                     Nonmagnetic          Composition                 Underlying                        Underlying                               Intermediate                                     Intermediate          (at. %) 120                 Layer 2c                        Layer 2c Film                               Layer 4                                     Layer 4 Film          angstroms ×                 Composition                        Thickness                               Composition                                     Thickness    Examples          two layers                 (at. %)                        (Angstrom)                               (at. %)                                     (Angstrom)    __________________________________________________________________________    25    Co78Pt11Cr11                 Cr98Mo2                        50     Cr98Mo2                                     50    26    "      "      100    "     "    27    "      "      50     "     "    28    "      "      "      "     "    29    "      Cr95Mo5                        50     Cr95Mo5                                     "    30    "      "      100    "     "    31    "      "      20     "     "    32    "      "      50     "     20    33    "      "      "      "     50    34    "      "      "      "     "    35    "      Cr90Mo10                        50     Cr90Mo10                                     50    36    "      "      100    "     "    37    "      "      20     "     "    38    "      "      50     "     20    39    "      "      "      "     50    40    "      "      "      "     "    41    "      Cr85Mo15                        50     Cr85Mo15                                     50    42    "      "      100    "     "    __________________________________________________________________________

                                      TABLE 4-2    __________________________________________________________________________          Substrate          Heating                Ar Gas    Mrδ          Temperature                Pressure  (memu/                               S/N Ratio                                     d.sub.(002) -d.sub.(100)    Examples          (° C.)                (mTorr)                     He(Oe)                          cm.sup.2)                               (dB)  (Angstrom)    __________________________________________________________________________    25    375   1.3  1950 0.97 35.7  +0.029    26    "     "    2000 0.94 35.9  +0.028    27    300   "    1850 0.95 35.0  +0.032    28    375   5.0  1900 0.96 35.3  +0.032    29    375   1.3  2050 1.00 37.1  +0.026    30    "     "    2100 0.96 37.3  +0.25    31    "     "    2000 0.94 37.0  +0.027    32    "     "    2000 1.00 37.1  +0.026    33    300   "    1950 0.96 36.3  +0.029    34    375   5.0  1950 0.97 36.3  +0.030    35    375   1.3  2000 1.0  36.7  +0.015    36    "     "    2050 0.96 36.9  +0.014    37    "     "    2000 0.93 36.8  +0.016    38    "     "    2000 1.00 36.7  +0.015    39    300   "    1950 0.97 36.5  +0.019    40    375   5.0  1950 0.96 36.3  +0.021    41    375   1.3  1950 0.99 35.5  +0.007    42    "     "    2000 1.02 35.6  +0.008    __________________________________________________________________________

                                      TABLE 5-1    __________________________________________________________________________          Magnetic Layer       Nonmagnetic                                      Nonmagnetic          Composition                 Underlying                        Underlying                               Intermediate                                      Intermediate          (at. %) 120                 Layer 2c                        Layer 2c Film                               Layer 4                                      Layer 4 Film          angstroms ×                 Composition                        Thickness                               Composition                                      Thickness    Examples          two layers                 (at. %)                        (Angstrom)                               (at. %)                                      (Angstrom)    __________________________________________________________________________    43    Co78Pt11Cr11                 Cr85Mo15                        20     Cr85Mo15                                      50    44    "      "      50     "      20    45    "      "      "      "      50    46    "      "      "      "      "    47    "      Cr80Mo20                        50     Cr80Mo20                                      50    48    "      "      "      "      "    49    "      "      "      "      "    50    "      Cr95Mo2Zr3                        "      Cr95Mo2Zr3                                      "    51    "      Cr92Mo6Zr2                        "      Cr92Mo6Zr2                                      "    52    "      Cr88Mo8Zr4                        "      Cr88Mo8Zr4                                      "    53    "      Cr83Mo12Zr5                        "      Cr83Mo12Zr5                                      "    __________________________________________________________________________

                                      TABLE 5-2    __________________________________________________________________________          Substrate          Heating                Ar Gas    Mrδ          Temperature                Pressure  (memu/                               S/N Ratio                                     d.sub.(002) -d.sub.(100)    Examples          (° C.)                (mTorr)                     He(Oe)                          cm.sup.2)                               (dB)  (Angstrom)    __________________________________________________________________________    43    375   1.3  1950 0.95 35.5  +0.007    44    "     "    1950 0.99 35.5  +0.007    45    300   "    1850 0.97 35.1  +0.013    46    375   5.0  1900 0.96 35.2  +0.011    47    375   1.3  1950 0.97 35.3  +0.002    48    300   "    1850 1.02 35.1  +0.005    49    375   5.0  1900 0.99 35.2  +0.004    50    "     1.3  2070 1.02 37.8  +0.028    51    "     "    2150 1.01 38.3  +0.025    52    "     "    2150 1.05 38.0  +0.021    53    "     "    2100 1.00 37.8  +0.016    __________________________________________________________________________

As are apparent from Tables 4 and 5, Examples 25 through 49 with theunderlying layer 2c and the nonmagnetic intermediate film 4 werecomposed of CrMo alloy and are excellent in coercive force (Hc), theproduct (Mrδ) of residual magnetization and film thickness, and thesignal-to-noise ratio. Examples 50 through 53 which have the underlyinglayer 2c of CrMoZr alloy and the nonmagnetic intermediate film 4 ofCrMoZr alloy are also excellent in coercive force (Hc), the product(Mrδ) of residual magnetization and film thickness, and thesignal-to-noise ratio. In particular, it has been found out thataddition of Zr to the CrMo alloy is helpful to further reduce noise andto improve the signal-to-noise ratio. To achieve such an effect, thecontent of Zr is preferably selected in a range between 2 and 5 at. %.

Examples 25 through 53 indicate that the differences (d.sub.(002)-d.sub.(110)) which represent relationships of the crystal latticespacings between the underlying CrMo layer 2c and the magnetic CoPtCrfilm 3 and between the nonmagnetic intermediate CrMo film 4 and themagnetic CoPtCr film 5 can be changed in dependency upon thecompositions of the underlying layer 2c, the compositions of thenonmagnetic intermediate film 4, the substrate heating temperature, andthe Ar gas pressure.

For example, Examples 25 through 53 to which a small amount of Mo wereadded, were excellent in the signal-to-noise ratio.

These results indicate that the content of Mo in the CrMo alloy used inthe underlying layer 2c and the nonmagnetic intermediate film 4 ispreferably restricted within a range between 2 and 20 at. % and servesto restrict the differences (d.sub.(002) -d.sub.(110)) to thepredetermined range mentioned above.

EXAMPLES 54 TO 70

Examples 54 to 70 were manufactured in a manner which is similar to thatof Example 25 except that the combination of the compositions of theunderlying CrMo layer and the nonmagnetic intermediate CrMo film 4 waschanged as shown in Table 6.

As in Examples 25 to 53, similar operational tests and measurements werecarried out in connection with Examples 54 to 70 also. It has beenconfirmed that Examples 54 to 70 have excellent properties like theother examples mentioned above, as shown in Table 6.

                                      TABLE 6-1    __________________________________________________________________________          Magnetic Layer       Nonmagnetic                                     Nonmagnetic          Composition                 Underlying                        Underlying                               Intermediate                                     Intermediate          (at. %) 120                 Layer 2c                        Layer 2c Film                               Layer 4                                     Layer 4 Film          angstroms ×                 Composition                        Thickness                               Composition                                     Thickness    Examples          two layers                 (at. %)                        (Angstrom)                               (at. %)                                     (Angstrom)    __________________________________________________________________________    54    Co78Pt11Cr11                 Cr98Mo2                        50     Cr95Mo2                                     50    55    "      "      "      Cr90Mo10                                     "    56    "      "      "      Cr80Mo20                                     "    57    "      Cr95Mo5                        "      Cr98Mo2                                     "    58    "      "      "      Cr90Mo10                                     "    59    "      "      "      Cr85Mo15                                     "    60    "      "      "      Cr80Mo20                                     "    61    "      Cr90Mo10                        "      Cr98Mo2                                     "    62    "      "      "      Cr95MoS                                     "    63    "      "      "      Cr85Mo15                                     "    64    "      "      "      Cr80Mo20                                     "    65    "      Cr85Mo15                        "      Cr98Mo2                                     "    66    "      "      "      Cr95Mo5                                     "    67    "      "      "      Cr90Mo10                                     "    68    "      Cr80Mo20                        "      Cr95Mo5                                     "    69    "      "      "      Cr90Mo10                                     "    70    "      "      "      Cr85Mo15                                     "    __________________________________________________________________________

                                      TABLE 6-2    __________________________________________________________________________                                    d.sub.(002) -d.sub.(100)                              d.sub.(002) -d.sub.(100)                                    (Angstrom)                              (Angstrom)                                    between                              between                                    Second                              First Magnetic        Substrate             Magnetic                                    Layer 5 and        Heating             Ar Gas   Mrδ                          S/N Layer 3 and                                    Nonmagetic    Exam-        Tempera-             Pressure (memu/                          Ratio                              Underlying                                    Intermediate    ples        ture (° C.)             (mTorr)                  He(Oe)                      cm.sup.2)                          (dB)                              Layer 2c                                    Layer 4    __________________________________________________________________________    54  375  1.3  1950                      0.97                          35.8                              +0.029                                    +0.026    55  "    "    2000                      0.97                          35.7                              "     +0.015    56  "    "    1900                      0.95                          35.1                              "     +0.002    57  "    "    2050                      0.98                          36.0                              +0.026                                    +0.029    58  "    "    2050                      1.00                          37.1                              "     +0.015    59  "    "    1950                      1.00                          36.5                              "     +0.007    60  "    "    1950                      1.02                          36.0                              "     +0.002    61  "    "    1950                      0.98                          36.1                              +0.015                                    +0.029    62  "    "    2000                      1.00                          37.0                              "     +0.026    63  "    "    2000                      0.99                          36.2                              "     +0.007    64  "    "    2000                      1.01                          36.0                              "     +0.002    65  "    "    1900                      1.00                          35.0                              +0.007                                    +0.029    66  "    "    1950                      0.99                          35.8                              "     +0.026    67  "    "    1950                      0.98                          35.5                              "     +0.015    68  "    "    1900                      0.98                          35.5                              "     +0.015    68  "    "    1900                      0.97                          35.5                              +0.002                                    +0.026    69  "    "    1900                      0.96                          35.4                              "     +0.015    70  "    "    1950                      0.98                          35.2                              "     +0.007    __________________________________________________________________________

As is apparent from Table 6, the coercive force (Hc), the product (Mrδ)of residual magnetization and film thickness, and the signal-to-noiseratio were improved when the underlying CrMo layer 2c which includes 2to 20 at. % of Mo is combined with the nonmagnetic intermediate CrMofilm 4. Practically, improvement of the signal-to-noise ratio has beenachieved by a combination of the underlying CrMo layer including 2 to 20at. % of Mo with the nonmagnetic intermediate CrMo film including S to10 at. % of Mo and another combination of the nonmagnetic intermediateCrMo film including 2 to 20 at. % of Mo with the underlying CrMo layerincluding 5 to 10 at. % of Mo. In addition, the most preferablecombination for improving the signal-to-noise ratio has been found to bea combination of the underlying CrMo layer including 5 to 10 at. % of Mowith the nonmagnetic intermediate CrMo film including 5 to 10 at. % ofMo.

EXAMPLES 71 THROUGH 88

Examples 71 through 80 were similar in structure to Example 25 exceptthat the composition of the magnetic film 3, the composition of theunderlying CrMo layer 2c, and the composition of the nonmagneticintermediate CrMo film 4 were modified in Examples 71 through 80, asshown in Table 7.

Likewise, Examples 81 through 88 were different from Example 25 in viewof the fact that the composition and the material of the magnetic film3, the composition of the underlying CrMo layer 2c, and the compositionof the nonmagnetic intermediate CrMo film 4 were varied in Examples 81to 88, as shown in Table 7.

The magnetic disks according to Examples 71 to 88 were tested andmeasured as in the other examples mentioned above. The test results andthe measurement results of Examples 71 to 88 are shown in Table 7 andare improved.

It is noted that, in Table 4, the difference (d.sub.(002) -d.sub.(110))obtained by subtracting the crystal lattice spacing of the (110) planesin the underlying CrMo layer 2c from the crystal lattice spacing of the(002) planes in the magnetic CoPtCr film 3 was equal to the difference(d.sub.(002) -d.sub.(110)) obtained by subtracting the crystal latticespacing of the (110) planes in the nonmagnetic intermediate CrMo film 4from the crystal lattice spacing of the (002) planes in the magneticCoPtCr film 5. This is because the underlying layer 2c, the nonmagneticintermediate film 4, the magnetic film 3, and the magnetic film 5 weredeposited under the same conditions. Taking this into consideration,Table 7 shows only one of two values obtained for each example.

                                      TABLE 7-1    __________________________________________________________________________         Magnetic Layer Underlying                               Nonmagnetic                                     Nonmagnetic         Composition                  Underlying                        Layer 2c                               Intermediate                                     Intermediate         (at. %) 120                  Layer 2c                        Film   Layer 4                                     Layer 4 Film    Exam-         angstroms × two                  Composition                        Thickness                               Composition                                     Thickness    ples layers   (at. %)                        (Angstrom)                               (at. %)                                     (Angstrom)    __________________________________________________________________________    71   Co84Pt5Cr11                  Cr95Mo5                        50     same as                                     50                               underlying                               layer 2c    72   "        Cr90Mo10                        "      same as                                     "                               underlying                               layer 2c    73   Co71Pt18Cr11                  Cr95Mo5                        "      same as                                     "                               underlying                               layer 2c    74   "        Cr90Mo10                        "      same as                                     "                               underlying                               layer 2c    75   Co54Pt11Cr5                  Cr9SMo5                        "      same as                                     "                               underlying                               layer 2c    76   "        Cr90Mo10                        "      same as                                     "                               underlying                               layer 2c    77   Co74Pt11Cr15                  Cr95Mo5                        "      same as                                     "                               underlying                               layer 2c    78   "        Cr90Mo10                        "      same as                                     "                               underlying                               layer 2c    79   Co64Pt11Cr25                  Cr95Mo5                        "      same as                                     "                               underlying                               layer 2c    80   "        Cr90Mo10                        "      same as                                     "                               underlying                               layer 2c    81   Co87Pt11Ta2                  Cr95Mo5                        "      same as                                     "                               underlying                               layer 2c    82   "        Cr90Mo10                        "      same as                                     "                               underlying                               layer 2c    83   Co76Pt11Cr11Ta2                  Cr95Mo5                        "      same as                                     "                               underlying                               layer 2c    84   "        Cr90Mo10                        "      same as                                     "                               underlying                               layer 2c    85   Co76Pt11Cr11Ta2                  Cr95Mo5                        "      same as                                     "                               underlying                               layer 2c    86   "        Cr90Mo10                        "      same as                                     "                               underlying                               layer 2c    87   Co73Pt11Cr11Ta5                  Cr95Mo5                        "      same as                                     "                               underlying                               layer 2c    88   "        Cr90Mo10                        "      same as                                     "                               underlying                               layer 2c    __________________________________________________________________________

                  TABLE 7-2    ______________________________________          Substrate          Heating   Ar Gas        Mrδ                                        S/N    Exam- Temperature                    Pressure      (memu/                                        Ratio                                             d.sub.(002) -d.sub.(100)    ples  (° C.)                    (mTorr) He(Oe)                                  cm.sup.2)                                        (dB) (Angstrom)    ______________________________________    71    375       1.3     1850  1.09  35.5 +0.001    72    "         "       1850  1.10  35.1 +0.003    73    "         "       2250  0.88  35.6 +0.032    74    "         "       2300  0.89  36.5 +0.24    75    "         "       1900  1.09  35.8 +0.031    76    "         "       1950  1.10  36.3 +0.022    77    "         "       2150  0.95  36.5 +0.020    78    "         "       2200  0.94  35.6 +0.010    79    "         "       2300  0.82  35.9 +0.013    80    "         "       2350  0.82  35.1 +0.003    81    "         "       1900  1.10  34.3 +0.028    82    "         "       1950  1.11  34.9 +0.020    83    "         "       1950  1.01  34.1 +0.032    84    "         "       1950  1.10  34.8 +0.024    85    "         "       2050  0.91  37.0 +0.028    86    "         "       2000  0.91  38.8 +0.018    87    "         "       2100  0.75  35.5 +0.030    88    "         "       2050  0.76  35.8 +0.021    ______________________________________

As is apparent from Table 7, a high Hc and a high signal-to-noise ratiocan be achieved when the underlying layer 2c and the nonmagneticintermediate film 4 are each composed of the CrMo alloy including 5 to10 at. % of Mo and the magnetic film is composed of the CoPtCr alloy(Examples 71 through 80) including 60 to 90 at. % of Co, 4 to 20 at. %of Pt, and 3 to 30 at. % of Cr.

Further improvement of He and the signal-to-noise ratio can be achievedby the use of the magnetic CoPtCr alloy film which includes 64 to 84 at.% of Co, 5 to 18 at. % of Pt, and 5 to 25 at. % of Cr.

When the magnetic layer is composed of the CoPtTa alloy (Examples 71through 84), a high Hc and a high signal-to-noise ratio can be achievedby inclusion of 80 to 90 at. % of Co, 5 to 15 at. % of Pt, and 1 to 7at. % of Ta.

When the magnetic film is composed of the CoPtCrTa alloy (Examples 85through 88), a high Hc and a high signal-to-noise ratio can be achievedby inclusion of 70 to 80 at. % of Co, 5 to 15 at. % of Pt, 5 to 25 at. %of Cr, and 1 to 7 at. % of Ta.

According to the results of the tests conducted by the presentinventors, Examples enumerated in Tables 4 through 7 were found to beimproved in over-writing properties.

In the method of manufacturing magnetic recording media according to thepresent invention, the underlying layer and the nonmagnetic intermediatefilms contacted with the magnetic films contain less impurities andcontaminants and, as a result, enable improvement of the magneticproperties, such as the coercive force, the reproduction output, and thesignal-to-noise ratio. In addition, the properties for the magneticrecording media can further be improved by reducing distribution of thedifference (d.sub.(002) -d.sub.(110)) ) between the crystal latticespacing described in the above.

What is claimed is:
 1. A method of manufacturing a magnetic recordingmedium by using a sputtering apparatus of an in-line type, said magneticrecording medium comprising a substrate, an underlying layer on saidsubstrate, and a magnetic layer which is deposited on said underlyinglayer and which has a first magnetic film comprising Co and Pt, anonmagnetic intermediate film including Cr, and a second magnetic filmcomprising Co and Pt, said underlying layer comprising a surface film incontact with said magnetic layer, said method comprising the stepof:depositing at least one of the surface film and the nonmagnetic filmby supplying a sputtering power between 100 and 1000 watts to asputtering chamber used for depositing said at least one of the surfacefilm and the nonmagnetic film in order to improve coercive force andsignal-to-noise ratio.